Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

• the invention relates to the manufacture of steel sheet, more particularly TRIP (Transformation Induced Plasticity) steel sheet, that is to say in which the steel exhibits plasticity induced by an allotropic transformation.
• TRIP Transformation Induced Plasticity
• TRIP steels have been developed that exhibit advantageous combinations of properties (strength/deformability). These properties are attributed to the structure of such steels, consisting of a ferrite matrix containing bainite and residual austenite phases. In hot-rolled sheet, the residual austenite is stabilized thanks to an increase in the content of elements such as silicon and aluminium, these elements retarding the precipitation of carbides in the bainite.
• Cold-rolled sheet made of TRIP steel is manufactured by reheating the steel, during the annealing, into a region where partial austenization occurs, followed by rapid cooling in order to avoid the formation of pearlite and then an isothermal soak in the bainite region: one portion of the austenite is converted to bainite while another portion is stabilized by the increase in carbon content of the residual austenite islands.
• the initial presence of ductile residual austenite is associated with a high deformability.
• the residual austenite of a part made of TRIP steel is progressively transformed to martensite, resulting in substantial hardening.
• a steel exhibiting TRIP behaviour therefore makes it possible to guarantee a high deformability and a high strength, these two properties usually being mutually exclusive. This combination provides the potential for high energy absorption, a quality typically sought in the automobile industry for impact-resistant parts.
• the object of the present invention is to solve the abovementioned problems.
• the subject of the invention is a composition for the manufacture of steel exhibiting TRIP behaviour, comprising, the contents being expressed by weight: 0.08% ⁇ C ⁇ 0.23%, 1% ⁇ Mn ⁇ 2%, 1 ⁇ Si ⁇ 2%, Al ⁇ 0.030%, 0.1% ⁇ V ⁇ 0.25%, Ti ⁇ 0.010%, S ⁇ 0.015%, P ⁇ 0.1%, 0.004% ⁇ N ⁇ 0.012%, and, optionally, one or more elements chosen from: Nb ⁇ 0.1%, Mo ⁇ 0.5%, Cr ⁇ 0.3%, the balance of the composition consisting of iron and inevitable impurities resulting from the smelting.
• the carbon content is such that: 0.08% ⁇ C ⁇ 0.13%.
• the carbon content is such that: 0.13% ⁇ C ⁇ 0.18%.
• the carbon content is such that 0.18% ⁇ C ⁇ 0.23%.
• the manganese content is such that: 1.4% ⁇ Mn ⁇ 1.8%.
• the manganese content satisfies the relationship: 1.5% ⁇ Mn ⁇ 1.7%.
• the silicon content is such that: 1.4% ⁇ Si ⁇ 1.7%.
• the aluminium content satisfies the relationship: Al ⁇ 0.015%.
• the vanadium content is such that: 0.12% ⁇ V ⁇ 0.15%.
• the titanium content is such that: Ti ⁇ 0.005%.
• the subject of the invention is also a sheet of steel of the above composition, the microstructure of which consists of ferrite, bainite, residual austenite and, optionally, martensite.
• the microstructure of the steel has a residual austenite content of between 8 and 20%.
• the microstructure of the steel preferably has a martensite content of less than 2%.
• the mean size of the residual austenite islands does not exceed 2 microns.
• the mean size of the residual austenite islands preferably does not exceed 1 micron.
• the subject of the invention is also a process for manufacturing a hot-rolled sheet exhibiting TRIP behaviour, in which:
• the temperature T er of the end of the hot rolling, the rate V c of the cooling and the temperature T coil of the coiling are chosen in such a way that the microstructure of the steel has a residual austenite content of between 8 and 20%.
• the temperature T er of the end of the hot rolling, the rate V c of the cooling and the temperature T coil of the coiling are chosen in such a way that the microstructure of the steel has a martensite content of less than 2%.
• the temperature T er of the end of the hot rolling, the rate V c of the cooling and the temperature T coil of the coiling are chosen in such a way that the mean size of the residual austenite islands does not exceed 2 microns, and very preferably is less than 1 micron.
• the subject of the invention is also a process for manufacturing a hot-rolled sheet exhibiting TRIP behaviour, in which:
• the coiling temperature T coil is below 400° C.
• the subject of the invention is also a process for manufacturing a cold-rolled sheet exhibiting TRIP behaviour, in which a hot-rolled steel sheet manufactured according to any one of the methods described above is supplied, the sheet is pickled, the sheet is cold-rolled, and the sheet is made to undergo an annealing heat treatment, the heat treatment comprising a heating phase at a heating rate V hs , a soak phase at a soak temperature T s for a soak time t s followed by a cooling phase at a cooling rate V cs when the temperature is below Ar3, followed by a soak phase at a soak temperature T′ s for a soak time t′ s , the parameters V hs , T s , t s , V cs , T′ s and t′ s being chosen in such a way that the microstructure of said steel consists of ferrite, bainite, residual austenite and, optionally, martensite.
• the parameters V hs , T s , t s , V cs , T′ s and t′ s are chosen in such a way that the microstructure of the steel has a residual austenite content of between 8 and 20%.
• the parameters V hs , T s , t s , V cs , T′ s and t′ s are chosen in such a way that the microstructure of the steel contains less than 2% martensite.
• the parameters V hs , T s , t s , V cs , T′ s and t′ s are chosen in such a way that the mean size of the residual austenite islands is less than 2 microns, very preferably less than 1 micron.
• the subject of the invention is also a process for manufacturing a cold-rolled sheet exhibiting TRIP behaviour according to which the sheet is made to undergo an annealing heat treatment, the heat treatment comprising a heating phase at a heating rate V hs of 2° C./s or higher, a soak phase at a soak temperature T s of between A c1 and A c3 for a soak time t s of between 10 and 200 s, followed by a cooling phase at a cooling rate V cs of greater than 15° C./s when the temperature is below Ar3, followed by a soak phase at a temperature T′ s of between 300 and 500° C. for a soak time t′ s of between 10 and 1000 s.
• the soak temperature T s is preferably between 770 and 815° C.
• the subject of the invention is also the use of a sheet of steel exhibiting TRIP behaviour, according to one of the embodiments described above, or manufactured by one of the processes described above, for the manufacture of structural components or of reinforcing elements in the automobile field.
• a bainitic transformation occurs from an austenitic structure formed at high temperature, and bainitic ferrite laths are formed. Owing to the very low solubility of carbon in ferrite compared with austenite, the carbon of the austenite is rejected between the laths. Thanks to certain alloying elements in the steel composition according to the invention, in particular silicon and manganese, the precipitation of carbides, especially cementite, hardly occurs. Thus, the interlath austenite becomes progressively enriched with carbon, without the precipitation of carbides occurring.
• the carbon content is between 0.08 and 0.23% by weight.
• the carbon content lies within a first range from 0.08 to 0.13% by weight.
• the carbon content is greater than 0.13% but does not exceed 0.18% by weight.
• the carbon content is within a third preferred range, in which this is greater than 0.18% but does not exceed 0.23% by weight.
• the minimum carbon content of each of the three preferred ranges makes it possible to achieve a minimum strength of 600 MPa, 800 MPa and 950 MPa on cold-rolled and annealed sheet, for each of the above respective ranges.
• the maximum carbon content of each of the three ranges makes it possible to guarantee satisfactory weldability, especially for spot welding, if the strength level obtained in each of these three preferred ranges is taken into account.
• manganese an element inducing the gamma phase, in an amount of between 1 and 2% by weight contributes to reducing the martensite start temperature M s and to stabilizing the austenite.
• This addition of manganese also participates in effective solid-solution hardening and therefore in increasing the strength.
• the manganese content is preferably between 1.4 and 1.8% by weight: in this way satisfactory hardening is combined with improved stability of the austenite, without correspondingly causing excessive hardenability in welded assemblies.
• the manganese content is between 1.5 and 1.7% by weight. In this way, the above desired effects are obtained without the risk of forming a deleterious banded structure, which would arise from any segregation of the manganese during solidification.
• the silicon content is preferably between 1.4 and 1.7% by weight.
• Aluminium is a very effective element for deoxidizing steel. Like silicon, it has a very low solubility in cementite and could be used in this regard to prevent the precipitation of cementite during a soak at a bainitic transformation temperature and to stabilize the residual austenite.
• the aluminium content does not exceed 0.030% by weight since, as will be seen below, very effective hardening is obtained by means of vanadium carbonitride precipitation.
• the aluminium content is greater than 0.030%, there is a risk of aluminium nitride precipitating, which correspondingly reduces the amount of nitrogen capable of precipitating with the vanadium.
• this amount is equal to 0.015% by weight or less, any risk of aluminium nitride precipitating is eliminated and the full effect of the hardening by the vanadium carbonitride precipitation is obtained.
• the titanium content does not exceed 0.010% by weight so as not to precipitate a significant amount of nitrogen in the form of titanium nitrides or carbonitrides. Owing to the high affinity of titanium for nitrogen, the titanium content preferably does not exceed 0.005% by weight. Such a titanium content therefore prevents the precipitation of (Ti,V)N in hot-rolled sheet.
• Vanadium and nitrogen are important elements in the invention.
• the inventors have demonstrated that, when these elements are present in the amounts defined according to the invention, they precipitate in the form of very fine vanadium carbonitrides associated with substantial hardening.
• vanadium content is less than 0.1% by weight or when the nitrogen content is less than 0.004% by weight, the precipitation of vanadium carbonitrides is limited and the hardening is insufficient.
• vanadium content is greater than 0.25% by weight or when the nitrogen content is greater than 0.012% by weight, the precipitation occurs at an early stage after the hot rolling in the form of coarser precipitates.
• the vanadium content is between 0.12 and 0.15% by weight, the uniform elongation or the elongation at break is particularly increased.
• Sulphur in an amount of more than 0.015% by weight, tends to precipitate excessively in the form of manganese sulfides that greatly reduce the formability.
• Phosphorus is an element known to segregate at grain boundaries. Its content must be limited to 0.1% by weight so as to maintain sufficient hot ductility and to promote failure by peel during tension-shear tests carried out on spot-welded assemblies.
• elements such as chromium and molybdenum, which retard the bainitic transformation and promote solid-solution hardening, may be added in amounts not exceeding 0.3 and 0.5% by weight, respectively.
• niobium may also be added in an amount not exceeding 0.1% by weight so as to increase the strength by complementary carbonitride precipitation.
• the sheet obtained is coiled at a temperature of 450° C. or below.
• the quasi-isothermal soak associated with this coiling operation results in the formation of a microstructure consisting of bainite, ferrite, residual austenite and, optionally, a small amount of martensite, and also leads to hardening vanadium carbonitride precipitation.
• the coiling temperature is 400° C. or below, the total elongation and the uniform elongation are increased.
• the temperature T er of the end of hot rolling, the cooling rate V c and the coiling temperature T coil will be chosen in such a way that the microstructure has a residual austenite content of between 8 and 20%.
• the amount of residual austenite is less than 8%, a sufficient TRIP effect cannot be demonstrated in mechanical tests.
• TRIP behaviour the residual austenite is progressively transformed to martensite during deformation, n being greater than 0.2, and necking occurs for higher strains.
• the residual austenite content is greater than 20%, the residual austenite formed under these conditions has a relatively low carbon content and is destabilized too easily during a subsequent deformation or cooling phase.
• V c and T coil are the more important ones:
• the parameters T er , V c and T coil will be chosen in such a way that the microstructure of the hot-rolled steel sheet contains less than 2% martensite. Otherwise, the elongation is reduced, as is the absorption energy corresponding to the area under the tensile stress-strain ( ⁇ - ⁇ ) curve.
• ⁇ - ⁇ tensile stress-strain
• the resulting mechanical behaviour approaches that of a dual-phase steel with a high initial value of the strain-hardening coefficient n, which decreases when the deformation ratio increases.
• the microstructure contains no martensite.
• V c and T coil parameters chosen for the purpose of obtaining a martensite content of less than 2%, the more important parameters are:
• the process starts with the manufacture of a hot-rolled sheet according to one of the variants presented above.
• the microstructures and mechanical properties obtained for the manufacturing process involving cold rolling and annealing which will be explained below, depend relatively little on the manufacturing conditions within the limits of the variants of the process that were explained above, in particular on variations in the coiling temperature T coil .
• the process for manufacturing cold-rolled sheet has the advantage of being largely insensitive to fortuitous variations in the conditions for manufacturing hot-rolled sheet.
• a coiling temperature of 400° C. or below will preferably be chosen, so as to keep more vanadium in solid solution, so as to be available for precipitation during the subsequent annealing of the cold-rolled sheet.
• the hot-rolled sheet is pickled using a process known per se, so as to give it a surface finish suitable for the cold rolling. This is carried out under standard conditions, for example by reducing the thickness of the hot-rolled sheet by 30 to 75%.
• An annealing treatment is then carried out suitable for recrystallizing the work-hardened structure and for giving the particular microstructure according to the invention.
• This treatment preferably carried out by continuous annealing, comprises the following successive phases:
• the sheet then undergoes rapid cooling at a rate V cs of greater than 15° C./s when the temperature is below Ar3. Rapid cooling when the temperature is below Ar3 is important so as to limit the formation of ferrite before the bainitic transformation. This rapid cooling phase when the temperature is below Ar3 may optionally be preceded by a slower cooling phase starting from the temperature T s .
• a soak at a temperature T′ s is carried out between 300° C. and 500° C. for a soak time t′ s of between 10 s and 1000 s. This therefore results in bainitic transformation and carbon enrichment of the residual austenite islands in such an amount that this residual austenite is stable even after cooling down to room temperature.
• the soak temperature T s is between 770 and 815° C.—there may be insufficient recrystallization below 770° C. Above 815° C., the fraction of intercritical austenite formed is too high and the hardening of the ferrite by vanadium carbonitride precipitation is less effective. This is because the intercritical ferrite content is less, as is the total amount of vanadium precipitated, vanadium being rather soluble in the austenite. Moreover, the vanadium carbonitride precipitates that form have a greater tendency to coarsen and to coalesce at high temperature.
• the sheet is made to undergo an annealing heat treatment, the parameters V hs , T s , t s , V s , T′ s , t′ s , of which are chosen in such a way that the microstructure of the steel obtained consists of ferrite, bainite and residual austenite, and optionally martensite.
• Advantageously parameters will be chosen such that the residual austenite content is between 8% and 20%. These parameters will preferably be chosen in such a way that the mean size of the residual austenite islands does not exceed 2 microns, and optimally does not exceed 1 micron. These parameters will also be chosen in such a way that the martensite content is less than 2%. Optimally, the microstructure contains no martensite.
• T s , t s , V cs and T′ s is more particularly important:
• the sheets manufactured according to the invention have a very high tensile strength of substantially above 800 MPa for a carbon content of about 0.22%.
• Their microstructure is composed of ferrite, bainite and residual austenite, together with martensite in an amount less than 2%.
• Inv3 10.8% residual austenite content
• the carbon concentration of the residual austenite islands is 1.36% by weight. This means that the austenite is sufficiently stable to obtain a TRIP effect as shown by the behaviour observed during the tensile tests carried out on these steel sheets.
• the sheet of reference steel R1 having a bainite-pearlite structure with a very low residual austenite content, does not exhibit TRIP behaviour. Its tensile strength is less than 800 MPa, i.e. a level considerably below that of the steels of the invention.
• Steel Inv2 according to the invention also has excellent toughness, since its ductile-brittle transition temperature ( ⁇ 35° C.) is considerably lower than that of the reference steel (0° C.).
• Hot-rolled sheets 3 mm in thickness of steels Inv2 and R1 manufactured according to Example 1 were cold rolled down to a thickness of 0.9 mm.
• An annealing heat treatment was then carried out, comprising a heating phase at a rate of 5° C./s, a soak phase at a soak temperature T s of between 775 and 815° C. (these temperatures lying within the A c1 -A c3 range) for a soak time of 180 s, followed by a first cooling phase at 6-8° C./s and then a cooling phase at 20° C./s in a range where the temperature is below Ar3, a soak phase at 400° C. for 300 s, in order to form bainite, and a final cooling phase at 5° C./s.
• microstructure thus obtained was observed, after etching with the Klemm etchant, which revealed the residual austenite islands.
• the mean size of these islands was measured by means of image analysis software.
• the mean island size was 1.1 microns.
• the general microstructure was finer, with a mean island size of 0.7 microns. Furthermore, these islands were more equiaxed in character. In particular, in the case of steel Inv2, these characteristics reduced the stress concentrations at the matrix/island interfaces.
• the mechanical properties after cold rolling and annealing are the following:
• Steel Inv2 manufactured according to the invention has a tensile strength of greater than 900 MPa. For a comparable soak temperature T s , its strength is considerably higher than that of the reference steel.
• the cold-rolled and annealed steels according to the invention have mechanical properties that are largely insensitive to small variations in certain manufacturing parameters, such as the coiling temperature and the annealing temperature T s .
• the invention makes it possible to manufacture steels exhibiting TRIP behaviour with an increased strength.
• Parts manufactured from steel sheet according to the invention are profitably used for the manufacture of structural components or reinforcing elements in the automotive field.

Landscapes

• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Heat Treatment Of Sheet Steel (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)

Applications Claiming Priority (4)

Publications (2)

Family

ID=35149545

Family Applications (1)

Country Status (14)

Families Citing this family (39)

Citations (14)

Family Cites Families (2)

• 2005
  • 2005-08-04 EP EP05291675A patent/EP1749895A1/fr not_active Withdrawn
• 2006
  • 2006-07-07 KR KR1020087005304A patent/KR101222724B1/ko active IP Right Grant
  • 2006-07-07 RU RU2008117135/02A patent/RU2403311C2/ru active
  • 2006-07-07 US US11/997,609 patent/US9732404B2/en active Active
  • 2006-07-07 KR KR1020127025650A patent/KR101232972B1/ko active IP Right Grant
  • 2006-07-07 ES ES06778838.0T patent/ES2515116T3/es active Active
  • 2006-07-07 CN CN2006800333766A patent/CN101263239B/zh active Active
  • 2006-07-07 BR BRPI0614391A patent/BRPI0614391B8/pt active IP Right Grant
  • 2006-07-07 UA UAA200805640A patent/UA92039C2/ru unknown
  • 2006-07-07 EP EP06778838.0A patent/EP1913169B1/fr active Active
  • 2006-07-07 MX MX2008001653A patent/MX2008001653A/es active IP Right Grant
  • 2006-07-07 JP JP2008524537A patent/JP5283504B2/ja active Active
  • 2006-07-07 CA CA2617879A patent/CA2617879C/fr active Active
  • 2006-07-07 WO PCT/FR2006/001668 patent/WO2007017565A1/fr active Application Filing
• 2008
  • 2008-02-01 MA MA30616A patent/MA29691B1/fr unknown
  • 2008-02-04 ZA ZA200801068A patent/ZA200801068B/xx unknown

Patent Citations (16)

Also Published As

Similar Documents

Legal Events